Dynamic high pressure process for fabricating superconducting and permanent magnetic materials

ABSTRACT

Shock wave formation of thin layers of materials with improved superconducting and permanent magnetic properties and improved microstructures. 
     The material fabrication system includes a sandwiched structure including a powder material placed between two solid members to enable explosive shock consolidation. The two solid members are precooled to about 80°-100° K. to reduce the residual temperatures attained as a result of the shock wave treatment, and thereby increase the quench rate of the consolidated powder.

The United States Government has rights in this invention pursuant toContract No. W-7405-ENG-48 between the U.S. Department of Energy and theUniversity of California, for the operation of Lawrence LivermoreNational Laboratory.

This is a division of application Ser. No. 937,794 filed Dec. 4, 1986,now U.S. Pat. No. 4,717,627.

FIELD OF THE INVENTION

This invention relates to preparation, using shock wave propagation, ofsolid materials with new superconducting and permanent magneticproperties.

BACKGROUND OF THE INVENTION

Certain solid materials manifest desirable electrical or magneticproperties when thin samples, of thicknesses from one micrometer(microns or μm) to ten millimeters (mm), are prepared and used. Oneproblem with some of these materials is that their preparation is notstraightforward, but requires slow and costly techniques and oftenproduces such materials in very small volume. The invention describedand claimed herein provides relatively inexpensive method and apparatusfor preparing these materials in reasonable volume.

SUMMARY OF THE INVENTION

One object of the invention is to provide method and apparatus to formmaterials of thickness a few microns or more that have saturationmagnetic fields of five kilo-oersteds or greater.

Another object is to provide method and apparatus to form new solidmaterials of thickness a few microns or more that have superconductingcritical magnetic fields of at least 150 kilogauss and may be embeddedin a metallic medium.

Other objects of the invention, and advantages thereof, will becomeclear by reference to the detailed description and the accompanyingdrawings.

To achieve the foregoing objects, in accordance with the invention, themethod in one embodiment (for powders) may comprise: providing threeplanar layers of materials, with layer #2 containing a powder containingone or more predetermined constituents and being contiguous to andpositioned between layers #1 and #3 along the two exposed planarsurfaces of #2, and with layers #1 and #3 being predetermined solidmetallic materials; providing a rigid planar surface contiguous with oneof the planar surfaces of layer #3 so that layer #3 lies between layer#2 and the rigid planar surface; providing a supersonic shock wave thatpasses through layers #1, #2 and #3 in that order; confining thethree-layer assembly on all sides so that the assembly withstandsboundary deformation pressures of up to 1 Megabar; allowing the powderin layer #2 to at least partially melt and coalesce into a higherdensity layer; and allowing the excess thermal energy in layer #2 torapidly flow into the adjacent layers #1 and #3.

The method in another embodiment (for films and bulk materials) maycomprise: providing three planar layers of materials, with layer #2containing a film or bulk material that contains one or morepredetermined constituents and is contiguous to and positioned betweenlayers #1 and #3 along the two exposed planar surfaces of #2, and withlayers #1 and #3 being predetermined solid metallic materials; providinga rigid planar surface contiguous with one of the planar surfaces oflayer #3 so that layer #3 lies between layer #2 and the rigid planarsurface; providing a supersonic shock wave that passes through layers#1, #2 and #3 in that order; confining the three-layer assembly on allsides so that the assembly withstands boundary deformation pressures ofup to 1 Megabar; and allowing the excess thermal energy in layer #2 torapidly flow into the adjacent layers #1 and #3.

DESCRIPTION OF THE DRAWINGS

FIG. 1 is a graphic view of calculated residual temperature, as afunction of maximum shock wave pressure, after passage of a shock wavethrough two representative materials, solid Cu and Fe powder (initialaverage density ρ=4.8 gm/cm³), both with initial temperature T=100° K.,where the Fe powder is assumed to be initially embedded in the Cu.

FIG. 2 is a graphic view of calculated cooling rate, at various depthsd, of a planar layer of Fe powder that has been compressed by passage ofa 0.5 Mbar shock wave through the Cu and the powder layer.

FIG. 3 is a schematic view of one embodiment of apparatus suitable forpracticing the invention for powder specimens.

FIG. 4 is a graphic view of pressure and density, as a function of time,sensed by a planar layer of Fe powder as a 0.5 Mbar shock wave passesfrom the Cu through the powder layer, initially 50 μm thick.

FIG. 5 is a graphical view of pressure versus time within a shockedCu-Fe powder-Cu sandwich or embedded Nb film, for two experiments atcalculated peak pressures of 0.74 Mbar and 0.98 Mbar (impact velocitiesof 2.76 and 3.38 km/sec, respectively), produced by a Cu impactor 1 mmthick. The structure in the pressure rise illustrated in FIG. 4 alsooccurs during the initial rise shown in FIG. 5, but the time scale istoo compressed to reveal this.

FIG. 6 is a schematic cutaway view of an alternative approach to shockwave generation in the powder layer, using a technique related toexplosive welding.

FIGS. 7 and 8 are schematic views of embodiments of apparatus suitablefor practicing the invention, using film (with a substrate) or bulkspecimens.

FIG. 9 is a schematic view of a second embodiment of apparatus suitablefor practicing the invention, using film or bulk specimens.

DETAILED DESCRIPTION

The invention relies in part on the following experimental observations,which are confirmed by theoretical calculations utilizing measured shockwave equation-of-state data: (1) When a metallic solid is compressed bya shock wave of given strength, the resulting rise in temperature isonly 10-20 percent of the resulting temperature rise where a powder ofthe same solid is compressed (and melted) by a shock wave of the samestrength; (2) Where a thin layer of metallic powder is compressed,heated and melted by a shock wave and the resulting mass is contiguouson at least one side with a metal layer at much lower temperature, themajority of heat loss or cooling of the higher temperature material willoccur by flow of heat to the contiguous metal layer rather than by flowto any adjacent material. As used herein, a "layer" of powder will referto either a thin sheet or a line of such powder. A shock wave propagatedthrough any powder with density of the order of 50 percent of soliddensity will produce a material of much higher temperature than thetemperature of the equivalently shocked solid material.

As an example, FIG. 1 exhibits the calculated residual temperature T_(r)(after pressure release) reached in shock-heated Fe powder, initially ofaverage density ρ=4.8 gm/cm³ and at temperature T₀ =100° K., and insolid Cu as a function of the maximum pressure P_(m) generated in thematerial by the shock wave. For P_(m) 0.47 Mbar in this Fe powderencapsulated in solid Cu, T_(r) exceeds T_(melt) (Fe)≈1800° K. and thepowder melts and coalesces. At this point, the temperature T_(r) insolid Cu may be approximately 300° K. The temperature T_(r) (Fe) isquenched by rapid temperature equilibration between the Fe and thecontiguous Cu.

FIG. 2 is a graphic view of calculated cooling rates (10⁶ -10⁹ ° K./sec)versus time for shock heated Fe powder (P_(max) =0.55 Mbar) contiguouswith solid Cu, for various depths d within the Fe material. At smallerdepths than d<5 μm within the Fe, the cooling rate may exceed 10⁹ °K./sec.; this rate peaks within a few hundred nanoseconds andsubsequently falls to a rate below the rates extant at greater depths.The high cooling rates available near the Fe-Cu interface in Fe arebelieved to produce fine-grain crystalline or amorphous Fe (or othermaterial) processed in this manner; this belief is based upon thefabrication of amorphous and fine-grain Fe alloys by the well-known meltspinning method, with a maximum quench rate of about 10⁶ ° K./sec. Thisfine-grain structure is required for superconductors with high criticalmagnetic fields and high critical electrical currents and for permanentmagnetic materials with high coercivities (≈five kilo-oersteds andgreater). The effectively uniaxial nature of the shock pressure pulseproduces a preferred crystalline orientation that is useful forproducing permanent magnetic materials. High temperatures are achievedin a confined specimen (constrained on all boundaries) at high pressureso that mixtures of materials with greatly differing volatilities can becombined without losing the more volatile constituents.

Superconducting materials for high magnetic fields and high electricalcurrent are embedded in a metallic medium (e.g., Cu or Al) in order toprovide thin, superconducting layers with sufficient strength towithstand the large electromagnetic forces present in a high fieldsuperconducting magnet and to provide a controlled, nondestructivecurrent path, if the material undergoes a transition fromsuperconducting state to normal state. The process described hereinembeds synthesised materials in a metallic matrix, and the resultingcomposite may then be used for high-field superconducting magnetapplications. This technique is also useful for synthesising newsuperconducting materials, using very fast thermal and pressure quenchrates.

One embodiment of apparatus to accomplish the dynamic high pressurecompaction and quenching of the powder, shown in FIG. 3, uses aprojectile 11 comprising a metal impactor 13 (Cu, Al, etc.) with aductile backing material 15 of plastic or other suitable material toattenuate the rearward-moving shock wave after impact. The plastic alsoserves to hold the metal impactor during the impactor's acceleration bya gas gun. The projectile 11 is initially caused to move at supersonicspeed toward a target 17 that includes a first substantially planarsheet 19 of Cu, Al, steel or similar material, and a parallel secondsolid planar sheet 21 of a similar material, with a thin planar layer orline 23 of the powder positioned between and contiguous with the solidlayers 19 and 21 as shown. Hereafter, the phrase "transverselycontiguous", applied to two or more planar layers of material, will meanthat these layers are parallel to and contiguous to one another along acommon plane that defines each of the planar layers. A strong back-uplayer 25, of steel or other suitable material, is positioned parallel toand transversely contiguous to the rear exposed surface of the secondsolid planar layer 21, in order to constrain layers 19, 21 and 23 attheir external boundaries and to dissipate part or all of the shock waveenergy after the wave passes once through the planar layers 19, 23 and21. As shown in FIG. 3, the back-up material 25 wraps around the sidesof layers 19, 21 and 23 to constrain lateral deformation. Lead or someother heavy material 26 is preferably positioned at the sides of thetarget adjacent to the plane of impact, leaving clearance for passage ofthe projectile, to prevent this surface from "blowing out" as thepressure waves travel outward from the impact area.

The projectile 11 impacts an exposed, parallel, planar surface of thefirst planar layer or sheet 19, at a velocity of substantially 0.2-4km/sec. The shock wave generated in the first planar layer movesprogressively through the powder layer 23, the second solid planar layer21 and the back-up layer 25; and the powder in layer 23 is melted andcaused to coalesce for sufficiently high shock pressures.

The powder layer 23 may initially have a material average density ofsubstantially 50 percent of theoretical solid density and may have athickness of 10-500 μm. The energy deposition time in the powder layeris small, 3-100 nsec., compared to the time, 100-500 nsec., that thepowder layer is held at the pressure to react chemically. The timeintervals that the powder materials are held at high temperatures andpressures may be controlled by varying the thickness and width of theimpactor plate. FIG. 4 indicates that, for initial powder layer densityρ₀ (Fe)=4.8 gm/cm³, the density after passage of the shock wave reachesρ(Fe)=9.2 gm/cm³ for a 0.55 Mbar pressure shock wave; this latterdensity is 1.2 times crystal density and may induce formation of a newsolid phase when the molten layer quenches to a solid state.

Alternatively, the embodiment shown in FIG. 3 may be replaced by one inwhich the first Cu layer 13 is positioned (stationary) at the target 17and the projectile 11 includes a planar impactor 41 of steel or othersuitable material, backed by a layer of a suitable high explosive 43that is detonated to move the projectile against the target, as shown inFIG. 6. By detonating the explosive at one end, a travelling detonationwave in the explosive generates a travelling pressure wave that forcesthe projectile plate against the target. In this manner, large lengthsor areas of such materials can be synthesized and embedded in Cu orother ductile material.

The bulk materials (e.g., Cu, Al, steel) surrounding and contiguous withthe powder may be 1-10 mm thick. These materials may be pre-cooled totemperatures of the order of 80°-100° K., to reduce the residualtemperature attained by such material after passage of the shock wavetherethrough and to thereby increase the powder-bulk materialtemperature difference and specimen temperature quench rate. Since theshock wave amplitude and residual temperature each attenuate as the wavemoves away from the impact area, pre-cooling also provides a heat sinkfor rapid cooling close to the specimen, irrespective of the residualshock temperature of the specimen. For certain applications, the initialtemperature may be increased to several hundred degrees Kelvin tosynthesize a new product at lower shock wave pressure and/or permitpost-shock annealing to achieve a desired grain size or microstructure.

For pressures that are less than required for complete melting of thepowder layer, shock powder particles will melt primarily on the surfacesthereof and fuse together when the interstitial regions quench to thesolid state. A fine-grain microstructure is required for superconductorswith high critical magnetic fields and high critical electricalcurrents, and for permanent magnetic materials with high coercivities(5-20 kilo-oersteds). These can be obtained by varying the shockpressure and temperature to vary crystallite chemical composition,structure, size and orientation, as well as the multiplicity of phasesinduced in the compacted powder. These features are important forpinning superconductor flux lines in superconductors and magnetic fluxlines in hard permanent magnets. Thus, shock wave pressures varying fromthe minimum required to barely compact a powder into a monolithic layer,up to that required to totally melt and thermally quench the powderparticles, are important for synthesis here. Suitable powder materialsfor preparing superconducting materials with high critical magneticfields include: Pb/Mo/S, Eu/Mo/S, Sn/Eu/Mo/S, Pb/Eu/Mo/S, La/Eu/Mo/S,Sn/Mo/S, Sn/Al/Mo/S, Nb/N, Mo/N, V/Si, Nb/Si, Nb/Ge, Nb/Al/Ge, Nb/Al,Nb/Ga, Nb/Ti and Nb/Zr. Suitable materials for preparation of permanentmagnetic material with high coercivity include: Sm/Co, Fe/B/x andFe/B/x/y, where the materials x and y are drawn from a group includingNd, Pr, Sm, Eu, Co and Ni.

FIG. 6 illustrates an alternative approach to generation of shock wavesin the powder layer, using a technique related to explosive welding oftwo plates. The purpose of this technique is to use explosives tofabricate arbitrarily long lengths or large areas of the desiredmaterial. One provides, as usual, a back-up plate 31 (steel or such) andan impact cushion layer 33 of Pb or similar high density material at theside of the impact area; first and second planar layers 39 and 35 of Cuor similar material, with a thin layer of powder 37 sandwiched betweenthese two layers; an impactor plate 41 spaced apart from the three-layersandwich 40; and a layer 43 of high explosive positioned to detonate anddrive the impactor plate against the three-layer sandwich 40. The highexplosive 43 is detonated at one end 43A, and the detonation frontproceeds toward the other end 43B. As the detonation front advanceslongitudinally from one end 43A to the other end 43B, successiveportions of the impactor plate are driven against the three-layersandwich, producing a rolling motion of impactor plate 41 against thesandwich 40. This produces a travelling high pressure shock wave in thelayers 35, 37 and 39 that again causes the layer 37 of powder particlesto partially or fully melt and to fuse together as desired. Thistechnique is used in explosive welding, where the object is to weld theimpactor plate and the adjacent plate together. Here, the object is todrive long lengths or large areas of the layers 35, 37 and 39 together;and the choice of shock wave pressures and other parameters may differfrom the choices for "pure" explosive welding.

We have performed dynamic compaction experiments on two representativepowder compounds, 51 weight percent Cu/49 weight percent Zr and Pb₁.2Mo₆ S₈, to assess the effect of shock pressure on the final structure ofthe material. For the Cu/Zr compound, 160 kbar shock pressure produced acompacted mixture, with some melting of the powder particle boundariesbut with some voids still showing; application of 600 kbar shockpressure produced a very fine grain structure with no trace of theoriginal individual powder particles. Application of 160 kbar shockpressure to the much harder Pb/Mo/S compound left large voids, with manyof the original powder particles being observable and little or nomelting of powder particle boundaries; shock pressure of 600 kbarproduced a fine grain structure and some evidence of melting, but withsome large voids.

The invention for processing films or bulk specimens relies in part onthe following observations, which are confirmed by experiments andtheoretical calculations utilizing measured shock wave equation-of-statedata.

(1) When a material is subjected to high pressure and temperature, it ispossible to induce a new crystal structure that is more stable at thehigher pressures and densities. If sufficiently high temperature is alsopresent, the rate of transformation to the new phase is increasedsubstantially; if the specimen can be quenched sufficiently quickly, ametastable, high pressure crystal will result. Because shock pressuresand the resulting temperature rises can be applied and releasedextremely quickly (in times less than a microsecond), shock waves areuseful for promoting irreversible (on shock wave time scale)transformations to synthesize and quench metastable materials.

(2) When a ductile metallic solid, such as Cu, Al, steel or similarmaterial, is compressed by a shock wave of a given strength, thismaterial is also heated by the shock wave. However, such materialsremain ductile at high pressure and do not undergo phase transitions atsuch pressures. Such materials can thus be used as capsules to containmaterials that are more brittle; these latter materials can beshock-synthesized to produce metastable superconducting or permanentmagnetic materials. The shock pressures and temperatures attained in theductile materials are comparable to the pressures and temperaturesattained in the more brittle specimens embedded in the ductilematerials.

(3) Maximum shock pressures and temperatures can be localized to thespecimen and the portion of the (ductile) capsule immediately adjacentto the specimen. As the shock wave moves away from the specimen, theshock heating attenuates with increasing distance and leaves thespecimen surrounded by a cooler heat sink region.

(4) When the maximum shock pressure of the specimen is released, thereversible portion of the shock internal energy is given up, and thespecimen temperature decreases at a rate up to 10⁹ ° K. per second. Theremaining thermal energy is removed quickly by thermal diffusion to thesurrounding heat sink.

(5) After the layer of superconducting or permanent magnetic material(the "specimen material") has been shock-compressed and heated in thismanner, some of the shock wave energy can be absorbed in an irreversibletransformation to a new phase of the material, with a correspondinglysmaller portion of the shock wave energy being available for dynamicheating of the material before flow of this heat to any contiguous layerof adjacent material.

(6) After removal of the shock wave pressure, the ductile material willrecover to substantially its original material state, but the specimenmaterial may retain its new state, with a new phase and possibly higherdensity than that of the original specimen material. In this manner,metastable materials can be shock synthesized.

As an example, FIG. 1 exhibits the calculated residual temperature T_(r)(after pressure release) reached in shock-heated solid Cu, initially attemperature T₀ =100° K., as a function of the maximum pressure P_(m)generated in the material by the shock wave. For Cu shocked at P_(m)=0.74 Mbar and 0.98 Mbar, the temperatures T_(r) are estimated at 500°K. and 800° K., respectively. Where a Nb film is shocked in a similarmanner, the temperatures T_(r) for P_(m) =0.74 Mbar and 0.98 Mbar areestimated as 650° K. and 1000° K., respectively.

The fast dynamic deformation process can produce a fine grain structurein the specimen material. This fine-grain structure is required forsuperconductors with high critical magnetic fields and high criticalelectrical currents and for permanent magnetic materials with highcoercivities (≈five kilo-oersteds and greater). The effectively uniaxialnature of the shock pressure pulse produces a preferred crystallineorientation that is useful for producing permanent magnetic materials.High temperatures are achieved in a confined specimen (constrained onall boundaries) at high pressure so that mixtures of materials withgreatly differing volatilities can be combined without losing the morevolatile constituents.

One embodiment of apparatus to subject films and bulk specimens todynamic high pressures, shown in FIGS. 7 and 8, uses a projectile 51comprising a metal impactor 53 (Cu, Al, etc.) with a ductile backingmaterial 55 of plastic or other suitable material to attenuate therearward-moving shock wave after impact. The plastic also serves to holdthe metal impactor during the impactor's acceleration by a gas gun. Theprojectile 51 is initially caused to move at supersonic speed toward atarget 57 that includes a first substantially planar sheet 59 of Cu, Al,steel or similar material, and a parallel second solid planar sheet 61of a similar material, with a planar layer of film or bulk material 63(and a film substrate 64 of Cu, steel, sapphire or such, where a filmspecimen is to be processed) of the specimen material positioned betweenand contiguous with the solid layers 59 and 61 as shown. A strongback-up layer 65, of steel or other suitable material, is positionedparallel to and transversely contiguous to the rear exposed surface ofthe second solid planar layer 61, in order to constrain layers 59, 61and 63 at their external boundaries and to dissipate part or all of theshock wave energy after the wave passes once through the planar layers59, 63 and 61. As shown in FIG. 7, the back-up material 65 wraps aroundthe sides of layers 59, 61, 63 and 64 to reduce lateral deformation.

The projectile 51 impacts an exposed, parallel, planar surface of thefirst planar layer or sheet 59, at a velocity of substantially 0.2-4km/sec. A shock wave generated in the first planar layer 59 movesprogressively through the layers 63, 61 and 65; and the specimenmaterial in layer 63 undergoes a permanent phase transition forsufficiently high pressures. An optional Pb block positioned to the sideprovides further stability.

The specimen material layer 63 may initially have a material averagedensity of substantially 100 percent of theoretical solid density andmay have a thickness of 1-10⁴ μm. The time intervals that the specimenmaterial is held at high temperatures and pressures may be controlled byvarying the thickness and width of the impactor plate.

The bulk materials (e.g., Cu, Al, steel) surrounding and contiguous withthe specimen material may be 0.1-10 mm thick or more. These materialsmay be pre-cooled to temperatures of the order of 80°-100° K., to reducethe residual temperature attained by such material after passage of theshock wave therethrough and to thereby increase the ductile-specimenmaterial temperature difference and specimen temperature quench rate.Because the shock wave amplitude and residual temperature each attenuateas the wave moves away from the impact area, pre-cooling also provides aheat sink for rapid cooling close to the specimen material, irrespectiveof the residual shock temperature of that material. For certainapplications, the initial temperature may be increased to severalhundred degrees Kelvin to synthesize a new product at lower shock wavepressure and/or permit post-shock annealing to achieve a desired grainsize or microstructure.

A fine-grain microstructure is required for superconductors with highcritical magnetic fields and high critical electrical currents, and forpermanent magnetic materials with high coercivities (5-20kilo-oersteds). These features are important for pinning superconductorflux lines in superconductors and magnetic flux lines in hard permanentmagnets. Suitable specimen materials for preparing superconductingmaterials with high critical magnetic fields include: Pb/Mo/S, Eu/Mo/S,Sn/Eu/Mo/S, Pb/Eu/Mo/S, La/Eu/Mo/S, Sn/Mo/S, Sn/Al/Mo/S, Nb/N, Mo/N,V/Si, Nb/Si, Nb/Ge, Nb/Al/Ge, Nb/Al, Nb/Ga, Nb/Ti and Nb/Zr. Suitablematerials for preparation of permanent magnetic material with highcoercivity include: Sm/Co, Fe/B/x and Fe/B/x/y, where the materials xand y are drawn from a group including Nd, Pr, Sm, Eu, Co and Ni.

FIG. 9 illustrates an alternative approach to generation of shock wavesin the specimen material layer, using a technique related to explosivewelding of two plates. One provides, as usual, a back-up plate 71 (steelor such) and an impact cushion layer 73 of Pb or similar high densitymaterial at the side of the impact area; first and second planar layers75 and 79 of Cu or similar material, with a layer of specimen material77 sandwiched between these two layers; an impactor plate 81 spacedapart from the three-layer sandwich 80; and a layer 83 of high explosivepositioned to detonate and drive the impactor plate against thethree-layer sandwich 80. The high explosive 83 is detonated at one end83A, and the detonation front proceeds toward the other end 83B. As thedetonation front advances longitudinally from one end 83A to the otherend 83B, successive portions of the impactor plate are driven againstthe three-layer sandwich, producing a rolling motion of impactor plate81 against the sandwich 80. This produces a travelling high pressureshock wave in the layers 75, 77 and 79 that again causes the layer 77 ofspecimen material to undergo a phase transition, as desired. Thistechnique is used in explosive welding, where the object is to weld theimpactor plate and the adjacent plate together. Here, the object is todrive the layers 75, 77 and 79 together; and the choice of shock wavepressures and other parameters may differ from the choices for "pure"explosive welding.

To demonstrate the method, apparatus similar to that indicated in FIG.8, has been applied to bulk polycrystalline Nb specimens, 13 mm indiameter by 9 mm thickness, at maximum shock pressures of 0.6 Mbar, 1.0Mbar and 1.2 Mbar. The critical temperature for manifestation ofsuperconductivity, T_(c), was found to decrease weakly with increasingshock pressure, from 9.18° K. for the unshocked specimen to 9.155° K. atthe highest shock pressure. Maximum increase of Vickers hardness, from75 (unshocked) to 130-150, was observed for the 0.6 Mbar specimen, andlong thin grain structures were induced in specimen planes perpendicularto the direction of propagation of the shock waves.

Next, several Nb films, each about 30 um thick, were depositedsimultaneously on Cu substrates that were 10 mm (diameter) by 1 mm(thickness). A Cu plate of 2.5 mm thickness was placed over the Nbfilms, and this target was subjected to shock waves induced with Cuimpactor velocities of 2.76 and 3.38 km/sec; these produced shockpressures of 0.74 Mbar and 0.98 Mbar, respectively. The higher impactorvelocity was chosen to produce a maximum pressure close to the pressure(0.9 Mbar) that is predicted to produce maximum shock-induced hardnessand defect concentration in the pure Nb film. Calculated shock wavepressure histories for the two experiments are those of FIG. 5. Forthese two situations, the predicted peak shock temperatures are 1200° K.and 1900° K., respectively; upon release of the material to zeropressure, these temperatures decrease to 850° K. and 1200° K.,respectively. The shock process is thermodynamically irreversible sothat the material temperature does not revert to room temperature afterthe pressure is released. The corresponding temperatures for the solidCu subtrate and capsule are lower than for Nb.

In these experiments, the first stage of cooling, which occurs uponisentropic release to the backing pressure provided by the plastic (≈0.2Mbar in FIG. 5), occurs in about 300 nsec; this corresponds to a bulkthermodynamic cooling rate of about 10⁹ ° K./sec. The second stage ofcooling occurs by conduction of heat from the Nb film to the contiguousCu substrate and capsule on two sides of the specimen and ductilematerial; the time required for this to occur is estimated at tens ofmicroseconds.

Optical photomicrographs of the Nb film embedded in the surrounding Cumaterial show a final Nb film thickness of about 20 um (reduced from 30um as a result of late-time plastic flow) with reasonably well definedNb-Cu interfaces for the 0.74 Mbar experiment. For the higher peakpressure of 0.98 Mbar, the Cu penetrates completely through the Nb filmat some locations; here the Cu recrystallizes to smaller grain size thanin the Cu substrate itself. The Nb specimens before and after the shocktreatment manifested substantially the same critical temperature, T_(c).Critical temperature for Nb is thus relatively insensitive to shocktreatment below one Mbar, but Vickers hardness is increased by about 100percent. This method allows access to previously-unexplored regions ofhigh density phase regions.

In the abovedescribed experiments with Nb, the superconductingtransition temperature is changed only modestly, about 0.1° K. out of9.4° K., by the shock process. The upper critical magnetic field H_(c2),however, is increased by a factor of about two over the correspondingfield for annealed Nb; thus is caused by the shock-induced defects.

Discs of Nb₃ Si, 1.5-2 mm thick and 12 mm in diameter and cut fromarc-melted buttons, were successfully recovered for applied shock wavepressures of 0.82 Mbar and 0.96 Mbar. The specimen subjected to 0.96Mbar pressure was found to contain a substantial amount of Al5-phase Nb₃Si with 5.09 A lattice parameter. The electrical resistance of theprocessed specimen goes abruptly to zero at temperature T_(c) =18° K.The specimen material retained its superconducting transition even afterpostshot "powdering", indicating that the superconductivity was inducedthroughout the bulk of the specimen. The electrical resistance of thespecimen shocked at 0.82 Mbar pressure did not completely vanish attemperature T=18° K.

An amorphous film of Nb₃ Si, shocked to 0.72 Mbar, was observed tocontain small (≲1000 A diameter) polycrystals of Al5-phase, which is thesuperconducting phase of this compound.

Although the preferred embodiments have been shown and described herein,variation and modification may be made without departing from the scopeof the invention.

We claim:
 1. A material fabrication system for preparation of a class offine grain solid materials having desirable superconducting or magneticproperties, the system comprising:a first planar layer of a firstpredetermined solid material; a second planar layer of a secondpredetermined solid material of thickness substantially between 1 μm and10 mm; a third planar layer of a third predetermined solid materialpositioned so that the second layer lies between the first layer and thethird layer and is traversely contiguous with the first layer; a fourthplanar layer of a fourth predetermined material, of thicknesssubstantially 10² -10⁴ μm, transversely contiguous with and positionedbetween said second planar layer and said third planar layer, to serveas a substrate for a film specimen in said second planar layer. an opencontainer for the first, second, third and fourth planar layers andhaving a first planar container wall, with the third layer beingtransversely contiguous with the first planar container wall and beingpositioned so that the third layer lies between the fourth layer and thefirst planar container wall, and with the container having side wallsthat fit snugly against the side walls of the first and third layers,the container being composed of rigid material that resists deformationcaused by deformation of the first layer or the third layer; shock wavemeans positioned adjacent to the first layer so that the first layerlies between the shock wave means and the second layer, to produce ashock wave in the first layer so that this shock wave propagatessubstantially transversely through the first layer, the second layer,the fourth layer and the third layer in that order, with the velocity ofpropagation of the shock wave being supersonic with respect to the speedof sound in each of the materials comprising the first, second, thirdand fourth planar layers.
 2. The system of claim 1 wherein the fourthplanar layer is formed of copper, steel or sapphire.
 3. The system ofclaim 1 wherein the first and third planar layers are formed of Cu, Alor steel and have a thickness of about 0.1-10 mm.
 4. A materialfabrication system for preparation of a class of fine grain solidmaterials having desirable superconducting or magnetic properties, thesystem comprising:a first planar layer of a first predetermined solidmaterial; a second planar layer of a second predetermined powdermaterial; a third planar layer of a third predetermined solid materialpositioned so that the second layer lies between and is transverselycontiguous with the first layer and the third layer; wherein the firstand third layers are precooled to about 80°-100° K. an open containerfor the first, second and third planar layers and having a first planarcontainer wall, with the third layer being transversely contiguous withthe first planar container wall and being positioned so that the thirdlayer lies between the second layer and the first planar container wall,and with the container having side walls that fit snugly against theside walls of the first and third layers, the container being composedof rigid material that resists deformation caused by deformation of thefirst layer or the third layer; shock wave means positioned adjacent tothe first layer so that the first layer lies between the shock wavemeans and the second layer, to produce a shock wave in the first layerso that this shock wave propagates substantially transversely throughthe first layer, the second layer and the third layer in that order,with the velocity of propagation of the shock wave being supersonic withrespect to the speed of sound in each of the materials comprising thefirst, second and third planar layers.
 5. The system according to claim4, wherein said second predetermined powder material for said secondlayer is chosen from the class of combinations consisting of: Pb/Mo/S,Eu/Mo/S, Sn/Eu/Mo/S; Pb/Eu/Mo/S, La/Eu/Mo/S, Sn/Mo/S, Sn/Al/Mo/S, Nb/N,Mo/N, V/Si, Nb/Si, Nb/Ge, Nb/Al/Ge, Nb/Al, Nb/Ga, Nb/Ti and Nb/Zr. 6.The system according to claim 4, wherein said second predeterminedpowder material for said second layer is chosen from the class ofcombinations consisting of: Sm/Co, Fe/B/Nd, Fe/B/Pr, Fe/B/Sm, Fe/B/Eu,Fe/B/Co, Fe/B/Ni, Fe/B/Nd/Pr, Fe/B/Nd/Sm, Fe/B/Nd/Eu, Fe/B/Nd/Co andFe/B/Nd/Ni.
 7. The system according to claim 4, wherein said third solidpredetermined material is drawn from the class consisting of Cu, Al andsteel.
 8. The system according to claim 4, further including a massiveblock of high density material that is positioned adjacent to said sidewalls of said first, second and third planar layers to provide stabilityfor said open container side walls.
 9. A material fabrication system forpreparation of a class of fine grain solid materials having desirablesuperconducting or magnetic properties, the system comprising:a firstplanar layer of a first predetermined solid material; a second planarlayer of a second predetermined solid material of thicknesssubstantially between 1 μm and 10 mm; a third planar layer of a thirdpredetermined solid material positioned so that the second layer liesbetween and is transversely contiguous with the first layer and thethird layer; wherein the first and third layers are precooled to about80°-100° K.; an open container for the first, second and third planarlayers and having a first planar container wall, with the third layerbeing transversely contiguous with the first planar container wall andbeing positioned so that the third layer lies between the second layerand the first planar container wall, and with the container having sidewalls that fit snugly against the side walls of the first and thirdlayers, the container being composed of rigid material that resistsdeformation caused by deformation of the first layer or the third layer;shock wave means positioned adjacent to the first layer so that thefirst layer lies between the shock wave means and the second layer, toproduce a shock wave in the first layer so that this shock wavepropagates substantially transversely through the first layer, thesecond layer and the third layer in that order, with the velocity ofpropagation of the shock wave being supersonic with respect to the speedof sound in each of the materials comprising the first, second and thirdplanar layers.
 10. The system according to claim 9, wherein said secondpredetermined material for said second layer is chosen from the class ofcombinations consisting of: Pb/Mo/S, Eu/Mo/S, Sn/Eu/Mo/S; Pb/Eu/Mo/S,La/Eu/Mo/S, Sn/Mo/S, Sn/Al/Mo/S, Nb/N, Mo/N, V/Si, Nb/Si, Nb/Ge,Nb/Al/Ge, Nb/Al, Nb/Ga, Nb/Ti and Nb/Zr.
 11. The system according toclaim 9, wherein said second predetermined powder material for saidsecond layer is chosen from the class of combinations consisting of:Sm/Co, Fe/B/Nd, Fe/B/Pr, Fe/B/Sm, Fe/B/Eu, Fe/B/Co, Fe/B/Ni, Fe/B/Nd/Pr,Fe/B/Nd/Sm, Fe/B/Nd/Eu, Fe/B/Nd/Co and Fe/B/Nd/Ni.
 12. The systemaccording to claim 9, wherein said third solid predetermined material isdrawn from the class consisting of Cu, Al and steel.
 13. The system ofclaim 4 wherein the first and third planar layers are ductile.
 14. Thesystem of claim 4 wherein the shock means produce a shock wave whichsimultaneously propagates longitudinally along the planes of the first,second and third layers while propagating substantially through thefirst, second and third layers.
 15. The system of claim 4 wherein thefirst and third layers are about 0.1-10 mm thick.
 16. The system ofclaim 9 wherein the first and third planar layers are ductile.
 17. Thesystem of claim 9 wherein the shock means produce a shock wave whichsimultaneously propagates longitudinally along the planes of the first,second and third layers while propagating substantially through thefirst, second and third layers.
 18. The system of claim 9 wherein thefirst and third layers are about 0.1-10 mm thick.